EP3186405A1 - Acier présentant une haute résistance à l'usure, une dureté élevée, une bonne résistance à la corrosion et/ou une faible conductivité thermique et utilisation d'un tel acier - Google Patents

Acier présentant une haute résistance à l'usure, une dureté élevée, une bonne résistance à la corrosion et/ou une faible conductivité thermique et utilisation d'un tel acier

Info

Publication number
EP3186405A1
EP3186405A1 EP15756892.4A EP15756892A EP3186405A1 EP 3186405 A1 EP3186405 A1 EP 3186405A1 EP 15756892 A EP15756892 A EP 15756892A EP 3186405 A1 EP3186405 A1 EP 3186405A1
Authority
EP
European Patent Office
Prior art keywords
steel
steel according
content
weight
particles
Prior art date
Legal status (The legal status is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the status listed.)
Granted
Application number
EP15756892.4A
Other languages
German (de)
English (en)
Other versions
EP3186405B1 (fr
Inventor
Horst HILL
André VAN BENNEKOM
Oliver RIPKENS
Current Assignee (The listed assignees may be inaccurate. Google has not performed a legal analysis and makes no representation or warranty as to the accuracy of the list.)
Deutsche Edelstahlwerke Specialty Steel GmbH and Co KG
Original Assignee
Deutsche Edelstahlwerke Specialty Steel GmbH and Co KG
Priority date (The priority date is an assumption and is not a legal conclusion. Google has not performed a legal analysis and makes no representation as to the accuracy of the date listed.)
Filing date
Publication date
Application filed by Deutsche Edelstahlwerke Specialty Steel GmbH and Co KG filed Critical Deutsche Edelstahlwerke Specialty Steel GmbH and Co KG
Publication of EP3186405A1 publication Critical patent/EP3186405A1/fr
Application granted granted Critical
Publication of EP3186405B1 publication Critical patent/EP3186405B1/fr
Active legal-status Critical Current
Anticipated expiration legal-status Critical

Links

Classifications

    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/18—Hardening; Quenching with or without subsequent tempering
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D1/00—General methods or devices for heat treatment, e.g. annealing, hardening, quenching or tempering
    • C21D1/26—Methods of annealing
    • C21D1/32—Soft annealing, e.g. spheroidising
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C29/00—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides
    • C22C29/005—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides comprising a particular metallic binder
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C29/00—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides
    • C22C29/02—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides
    • C22C29/06—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides based on carbides, but not containing other metal compounds
    • C22C29/10—Alloys based on carbides, oxides, nitrides, borides, or silicides, e.g. cermets, or other metal compounds, e.g. oxynitrides, sulfides based on carbides or carbonitrides based on carbides, but not containing other metal compounds based on titanium carbide
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/02—Making ferrous alloys by powder metallurgy
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/02—Making ferrous alloys by powder metallurgy
    • C22C33/0257—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements
    • C22C33/0278—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5%
    • C22C33/0285—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5% with Cr, Co, or Ni having a minimum content higher than 5%
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C33/00—Making ferrous alloys
    • C22C33/02—Making ferrous alloys by powder metallurgy
    • C22C33/0257—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements
    • C22C33/0278—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5%
    • C22C33/0292—Making ferrous alloys by powder metallurgy characterised by the range of the alloying elements with at least one alloying element having a minimum content above 5% with more than 5% preformed carbides, nitrides or borides
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/42—Ferrous alloys, e.g. steel alloys containing chromium with nickel with copper
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/44—Ferrous alloys, e.g. steel alloys containing chromium with nickel with molybdenum or tungsten
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/50—Ferrous alloys, e.g. steel alloys containing chromium with nickel with titanium or zirconium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/18—Ferrous alloys, e.g. steel alloys containing chromium
    • C22C38/40—Ferrous alloys, e.g. steel alloys containing chromium with nickel
    • C22C38/52—Ferrous alloys, e.g. steel alloys containing chromium with nickel with cobalt

Definitions

  • the invention relates to a steel for uses requiring high wear resistance, high hardness, good corrosion resistance and / or low thermal conductivity.
  • Cutting tools perforated plates, sieves, molds and similar components for machines needed in the plastics processing industry.
  • a typical field of application here are machines for the regeneration or recycling of plastic products, which are melted down into a melt for their return into the processing cycle.
  • the melt is forced through a perforated plate, from which it emerges in a large number of single strands.
  • the single strands solidify and then by means of suitable, near the perforated plate rotating knives to individual granules
  • the perforated plates used must have a good corrosion resistance due to the corrosive environment in which they are exposed in use and are exposed to high abrasive wear. Especially for the
  • a known steel intended for this purpose is known under the material number 1.2379 (AISI designation: D2). It contains besides iron and unavoidable Impurities (in wt%) 1.55% C, 12.00% Cr, 0.80 Mo and 0.90% V.
  • Material number 1.3343 (AISI designation: M2) standardized. It contains besides iron and unavoidable
  • Impurities (in wt%) 0.85-0.9% C, 0.25% Mn, 4.1% Cr, 5.0% Mo, 1.9% V and 6.4% W.
  • the highest demands on wear are to be met by the martensitic steel standardized under the material number 1.4110 (AISI designation: 440A), which in addition to iron and unavoidable impurities (in% by weight) 0.6 - 0.75% C, max. 1% Mn, max. 1% Si, max. 0.04% P, max. 0.03% S, 16 - 18% Cr and max. 0.75% Mo contains.
  • This steel achieves a hardness of at least 60 HRC after a suitable heat treatment.
  • a steel known under the trade designation "Ferro-Titanit Nikro 128" which has been specially created for the manufacture of components used in the processing of abrasive plastics, contains besides iron and unavoidable impurities (in% by weight) 13 , 5% Cr, 9% Co, 4% Ni and 5% Mo.
  • the proportion of titanium carbide in the structure of the composite steel is 30 wt .-%, which corresponds to a volume fraction of about 40 vol .-% TiC.
  • the well-known powder metallurgy produced steel achieved after over two to four hours under vacuum annealing at 850 ° C and a subsequent deterrence, in which he was a
  • a subsequent curing treatment in which the steel over six to eight hours at 480 ° C, to a maximum hardness of about 62 HRC can be increased.
  • From this steel are typically perforated plates, granulators, spray nozzles and
  • Screws, rings and other pressing tools for the processing of abrasive plastics as well as components for pumps, filling heads and ring knives, which are required for canning-filling machines see data sheet "Ferro-Titanit Nikro 128"
  • the object of the invention was to provide a steel which is in the
  • the invention provides a steel for applications requiring high wear resistance, high hardness, good corrosion resistance and / or low thermal conductivity.
  • the steel according to the invention achieves a hardness of at least 56 HRC in the cured state and contains in its structure a total of at least 30% by weight of hard phases
  • TiC particles of carbide, Oxide or nitride particles present in addition to the TiC particles of carbide, Oxide or nitride particles exist.
  • the content of TiC particles is
  • the hard phases are in a matrix
  • a steel according to the invention is particularly suitable for the production of components for
  • Hole openings are made microfine to produce correspondingly finely granulated granules.
  • knives for shredding of steel according to the invention can be made
  • a steel according to the invention contains at least 20% by weight of TiC embedded in a matrix which is penetrated by
  • Deterioration contributes to the hardenability of the steel and at the same time is chosen so that a low
  • Thermal conductivity of less than 35 W / mK is guaranteed regardless of the respective heat treatment state.
  • the passive current density of the steel according to the invention is less than 5 ⁇ / cm 2 , measured in oxygen-free 0.5 molar sulfuric acid with a
  • Wear resistance has a corrosion resistance comparable to the corrosion resistance
  • steels is at a temperature of 20 ° C at more than 270 GPa, in particular more than 300 GPa, so that the steel according to the invention or produced therefrom
  • Coefficient of expansion of steel according to the invention is that for applications for the steels according to the invention
  • the steel according to the invention contains at least 20% by weight, corresponding to about 30% by volume of TIC, or at least 28% by weight of TiC, in particular at least 30% by weight of TiC.
  • the TiC content should not exceed an upper limit of 45% by weight. That way you can ensure that yourself
  • Too high a hard phase content leads to increased hardness and wear resistance.
  • a steel according to the invention also contributes that According to the invention further hard phases are present in addition to the TiC particles in the steel matrix, so that the volume fraction of the hard phases in the structure of the steel is at least 30 wt .-% in total. This can be done by separate addition of carbide, nitride or oxide particles in the production of the steel. Alternatively or additionally, the elements forming the weight fractions of the precipitates (Ni, Al, Ti) can also be used within the
  • form steel according to the invention are intermetallic precipitates, in whose formation mainly the elements Ni, Al and Ti are involved. These elements form Ni 3 Al and Ni 3 Ti or mixed forms. These intermetallic phases are present in the structure with grain sizes of the order of 10 nm and are not counted to the total hard phase content. Due to their small size, they afford the
  • intermetallic precipitations an increase in hardness and strength of the metal matrix and thus also contribute to improving the performance properties.
  • Chromium is in the steel of the invention in levels of
  • the Cr content is 12.5-14.5 wt .-%.
  • Molybdenum is contained in the steel according to the invention in amounts of 5.0-9.0 wt .-%, on the one hand to ensure sufficient corrosion resistance, in particular with regard to pitting corrosion and on the other hand to support the formation of intermetallic phases, by the hardness of the steel matrix, in which the hard phases are embedded, is increased.
  • the Mo content of the steel according to the invention is 6.5-7.5% by weight.
  • Cobalt is contained in the steel according to the invention in contents of 6.0 - 11.0 wt .-%, in order to To increase martensite start temperature and on the other hand to reduce the solubility of Mo in the metal matrix. In this way, in the inventive
  • the Co content of the steel according to the invention is 8.0-10.0% by weight
  • Copper is in the steel of the invention in contents of
  • the Cu content of the steel according to the invention is 0.5-1.0% by weight.
  • Nickel is in the steel according to the invention in contents of
  • Nickel is needed in the steel matrix in sufficient quantity to be at a
  • the presence of nickel stabilizes the austenite to such an extent that martensite is safely formed during quenching. If too little nickel is present in the steel matrix provided according to the invention, this effect is not achieved with the necessary certainty. If, on the other hand, too much nickel is present in the steel matrix, no martensite forms, since the austenitic phase is then stable even at room temperature.
  • the second object of nickel in the steel according to the invention is precipitation hardening by formation of intermetallic phases with elements such as Al and Ti. Therefore, in the steel matrix of the invention Steel the contents of Ni, Al and Ti on each other
  • Titanium is in the steel according to the invention in contents of
  • the Ti content of the steel according to the invention is 0.8 to 1.2% by weight.
  • aluminum is contained in the steel of the present invention at levels of 0.1-2.0% by weight to effect precipitation hardening in combination with Ni.
  • the Al content of the steel according to the invention is 1.0 to 1.4% by weight.
  • the steel according to the invention can be hardened with extremely low distortion, since titanium carbide has a low thermal expansion and no transformation.
  • the wear resistance of the steel according to the invention is increased.
  • the NbC particles have a lower thermal conductivity than TiC, which is beneficial to the
  • Tic and NbC are isomorphic carbides and therefore miscible with each other. This leads to
  • the carbide, nitride and oxide particles used according to the invention as hard phases are already supplied as "finished” particles during powder metallurgical production.
  • both the sintering, as well as the HIP (hot isostatic pressing) route can be used.
  • this is also suitable
  • the steel according to the invention can be used to adjust its mechanical properties to a conventional one
  • Steel according to the invention regularly has a hardness of more than 62 HRC after such a heat treatment.
  • Steel according to the invention has a hardness of more than 50 HRC.
  • the invention is based on
  • Fig. 1 shows a detail of a
  • FIG. 2 is a diagram in which the results of
  • Fig. 3 is a diagram with the result of an
  • composition of the steel V corresponded to the composition of the known under the name "Ferro-Titanit Nikro 128", for example, in the above-mentioned publication documented steel.
  • the completed in the powder metallurgical production of both steels E, V operations corresponded to the
  • Heat treatment corresponded.
  • samples PE1 and PV1 were first kept in vacuo at a temperature of 850 ° C. for a period of two to four hours and then quenched under a nitrogen atmosphere pressurized with 1 to 4.5 bar. This is followed by a curing treatment in which the samples PEl, PVl have been stored for six to eight hours at a temperature of 480 ° C.
  • Fig. 1 shows a section of a
  • Metal matrix is recognizable by the bright areas, whereas the TiC inclusions surrounded by the matrix are rendered dark.
  • the hard phase contents were determined on the samples PE1, PV1, PE2, PV2. They were with the from the
  • Comparative steel V produced samples PV1, PV2 had on average only 30 wt .-% hard phases.
  • PEl, PE2, PVl, PV2 five hardness measurements according to DIN EN ISO 6508-1 were carried out.
  • the mean values of the measured values thus acquired for the samples PE1, PE2, PV1, PV2 are in
  • the TiC content of the samples according to the invention PE1, PE2 was, as indicated in Table 1, each more than 30 wt .-%.
  • the modulus of elasticity is determined by means of ultrasound in FIG.
  • PV1 was 294 GPa.
  • FIG. 4 shows, by way of example, the result of a dilatometer measurement on a sample PE 1 produced from the steel according to the invention, which confirms this result.

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  • Chemical & Material Sciences (AREA)
  • Engineering & Computer Science (AREA)
  • Materials Engineering (AREA)
  • Mechanical Engineering (AREA)
  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
  • Thermal Sciences (AREA)
  • Crystallography & Structural Chemistry (AREA)
  • Powder Metallurgy (AREA)
  • Manufacture Of Metal Powder And Suspensions Thereof (AREA)
  • Heat Treatment Of Articles (AREA)
  • Heat Treatment Of Steel (AREA)
  • Heat Treatment Of Sheet Steel (AREA)

Abstract

L'invention concerne un acier qui peut être produit de façon fiable à l'échelle industrielle et qui est destiné à des applications qui nécessitant une haute résistance à l'usure, une dureté élevée, une bonne résistance à la corrosion et/ou une faible conductivité thermique. La dureté d'un acier de l'invention est d'au moins 56 HRC à l'état durci. Pour cela, la structure de l'acier contient au total au moins 30% en poids de phases dures qui sont constituées, en plus des particules de TiC, d'autres particules de carbure, particules d'oxyde ou particules de nitrure. La teneur en particules de TiC dans l'acier de l'invention est d'au moins 20% en poids. Les particules de phase dure sont incorporées dans une matrice constituée (% en poids) de 9,0 à 15,0% de Cr, de 5,0 à 9,0% de Mo, de 3,0 à 7,0% de Ni, de 6,0 à 11,0% de Co, de 0,3 à 1,5% de Cu, de 0,1 à 2,0% de Ti, de 0,1 à 2,0% d'Al, le reste étant du fer et des impuretés inévitables. Sa combinaison de propriétés rend l'acier de l'invention particulièrement approprié à la production de composants, en particulier de couteaux ou de plaques perforées qui sont nécessaires dans la production et le recyclage de matières plastiques.
EP15756892.4A 2014-08-28 2015-08-26 Acier présentant une haute résistance à l'usure, une dureté élevée, une bonne résistance à la corrosion et/ou une faible conductivité thermique et utilisation d'un tel acier Active EP3186405B1 (fr)

Applications Claiming Priority (2)

Application Number Priority Date Filing Date Title
DE102014112374.3A DE102014112374A1 (de) 2014-08-28 2014-08-28 Stahl mit hoher Verschleißbeständigkeit, Härte und Korrosionsbeständigkeit sowie niedriger Wärmeleitfähigkeit und Verwendung eines solchen Stahls
PCT/EP2015/069477 WO2016030396A1 (fr) 2014-08-28 2015-08-26 Acier présentant une haute résistance à l'usure, une dureté élevée, une bonne résistance à la corrosion et/ou une faible conductivité thermique et utilisation d'un tel acier

Publications (2)

Publication Number Publication Date
EP3186405A1 true EP3186405A1 (fr) 2017-07-05
EP3186405B1 EP3186405B1 (fr) 2018-10-03

Family

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Application Number Title Priority Date Filing Date
EP15756892.4A Active EP3186405B1 (fr) 2014-08-28 2015-08-26 Acier présentant une haute résistance à l'usure, une dureté élevée, une bonne résistance à la corrosion et/ou une faible conductivité thermique et utilisation d'un tel acier

Country Status (9)

Country Link
US (1) US20180119257A1 (fr)
EP (1) EP3186405B1 (fr)
JP (1) JP6210502B1 (fr)
KR (1) KR20170041276A (fr)
CN (1) CN107075624A (fr)
BR (1) BR112017002127A2 (fr)
DE (1) DE102014112374A1 (fr)
RU (1) RU2674174C2 (fr)
WO (1) WO2016030396A1 (fr)

Families Citing this family (5)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
EP3263726A1 (fr) * 2016-06-29 2018-01-03 Deutsche Edelstahlwerke GmbH Matériau à base de fe et son procédé de fabrication
JP7287916B2 (ja) * 2020-03-12 2023-06-06 株式会社神戸製鋼所 積層造形物の製造方法、及び積層造形物
CN111455274A (zh) * 2020-04-08 2020-07-28 鞍钢股份有限公司 一种80Ksi级别9Cr火驱热采油井管及其制造方法
CN112251749B (zh) * 2020-10-23 2023-04-07 黑龙江科技大学 一种利用等离子熔覆制备定向阵列的陶瓷相增强高熵合金耐磨涂层的方法
KR20220063626A (ko) * 2020-11-10 2022-05-17 한국재료연구원 TiC 입자 강화 Fe계 복합재료 및 그 제조방법

Family Cites Families (14)

* Cited by examiner, † Cited by third party
Publication number Priority date Publication date Assignee Title
US3966423A (en) * 1973-11-06 1976-06-29 Mal M Kumar Grain refinement of titanium carbide tool steel
DE3015709A1 (de) * 1980-04-24 1981-10-29 Thyssen Edelstahlwerke AG, 4000 Düsseldorf Hartstofflegierung
JPH0229736B2 (ja) * 1984-09-14 1990-07-02 Mitsubishi Metal Corp Bunsankyokagatashoketsugokinkoseinetsukantaimamobuzai
JPH0586435A (ja) * 1991-09-27 1993-04-06 Hitachi Metals Ltd 高耐食高耐摩耗性工具部品材料
SE9604538D0 (sv) * 1996-12-10 1996-12-10 Hoeganaes Ab Agglomerated iron-based powders
JP4279935B2 (ja) * 1999-03-25 2009-06-17 株式会社神戸製鋼所 硬質粒分散焼結鋼及びその製造方法
US6521353B1 (en) * 1999-08-23 2003-02-18 Kennametal Pc Inc. Low thermal conductivity hard metal
SE529041C2 (sv) * 2005-08-18 2007-04-17 Erasteel Kloster Ab Användning av ett pulvermetallurgiskt tillverkat stål
SE528991C2 (sv) * 2005-08-24 2007-04-03 Uddeholm Tooling Ab Ställegering och verktyg eller komponenter tillverkat av stållegeringen
GB2440737A (en) * 2006-08-11 2008-02-13 Federal Mogul Sintered Prod Sintered material comprising iron-based matrix and hard particles
SE533988C2 (sv) * 2008-10-16 2011-03-22 Uddeholms Ab Stålmaterial och förfarande för framställning därav
AU2011213543A1 (en) * 2010-02-05 2012-08-30 Weir Minerals Australia Ltd Hard metal materials
RU2443795C2 (ru) * 2010-04-16 2012-02-27 Тамара Федоровна Волынова МНОГОФУНКЦИОНАЛЬНЫЕ АНТИФРИКЦИОННЫЕ НАНОСТРУКТУРИРОВАННЫЕ ИЗНОСОСТОЙКИЕ ДЕМПФИРУЮЩИЕ С ЭФФЕКТОМ ПАМЯТИ ФОРМЫ СПЛАВЫ НА МЕТАСТАБИЛЬНОЙ ОСНОВЕ ЖЕЛЕЗА СО СТРУКТУРОЙ ГЕКСАГОНАЛЬНОГО ε-МАРТЕНСИТА И ИЗДЕЛИЯ С ИСПОЛЬЗОВАНИЕМ ЭТИХ СПЛАВОВ С ЭФФЕКТОМ САМООРГАНИЗАЦИИ НАНОСТРУКТУРНЫХ КОМПОЗИЦИЙ, САМОУПРОЧНЕНИЯ И САМОСМАЗЫВАНИЯ ПОВЕРХНОСТЕЙ ТРЕНИЯ, С ЭФФЕКТОМ САМОГАШЕНИЯ ВИБРАЦИЙ И ШУМОВ
EP2662460A1 (fr) * 2012-05-07 2013-11-13 Valls Besitz GmbH Traitements thermiques bainitiques résistants sur des aciers pour outillage

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Publication number Publication date
RU2017106319A3 (fr) 2018-08-28
DE102014112374A1 (de) 2016-03-03
WO2016030396A1 (fr) 2016-03-03
JP2017532434A (ja) 2017-11-02
CN107075624A (zh) 2017-08-18
RU2674174C2 (ru) 2018-12-05
EP3186405B1 (fr) 2018-10-03
KR20170041276A (ko) 2017-04-14
BR112017002127A2 (pt) 2017-11-21
JP6210502B1 (ja) 2017-10-11
RU2017106319A (ru) 2018-08-28
US20180119257A1 (en) 2018-05-03

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